EP3778976A1 - Panneau composite en acier inoxydable double paroi de haute résistance et son procédé de fabrication - Google Patents

Panneau composite en acier inoxydable double paroi de haute résistance et son procédé de fabrication Download PDF

Info

Publication number
EP3778976A1
EP3778976A1 EP19803939.8A EP19803939A EP3778976A1 EP 3778976 A1 EP3778976 A1 EP 3778976A1 EP 19803939 A EP19803939 A EP 19803939A EP 3778976 A1 EP3778976 A1 EP 3778976A1
Authority
EP
European Patent Office
Prior art keywords
stainless steel
steel clad
substrate layer
sided
layer
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Pending
Application number
EP19803939.8A
Other languages
German (de)
English (en)
Other versions
EP3778976A4 (fr
Inventor
Zhiyu Wang
Sihai JIAO
Shaoming QIANG
Huawei ZHANG
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Baoshan Iron and Steel Co Ltd
Original Assignee
Baoshan Iron and Steel Co Ltd
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Baoshan Iron and Steel Co Ltd filed Critical Baoshan Iron and Steel Co Ltd
Publication of EP3778976A1 publication Critical patent/EP3778976A1/fr
Publication of EP3778976A4 publication Critical patent/EP3778976A4/fr
Pending legal-status Critical Current

Links

Images

Classifications

    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B32—LAYERED PRODUCTS
    • B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
    • B32B15/00—Layered products comprising a layer of metal
    • B32B15/01—Layered products comprising a layer of metal all layers being exclusively metallic
    • B32B15/011—Layered products comprising a layer of metal all layers being exclusively metallic all layers being formed of iron alloys or steels
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/38—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling sheets of limited length, e.g. folded sheets, superimposed sheets, pack rolling
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B32—LAYERED PRODUCTS
    • B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
    • B32B15/00—Layered products comprising a layer of metal
    • B32B15/01—Layered products comprising a layer of metal all layers being exclusively metallic
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0273—Final recrystallisation annealing
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/50—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for welded joints
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C33/00—Making ferrous alloys
    • C22C33/04—Making ferrous alloys by melting
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/002—Bainite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/009—Pearlite

Definitions

  • the present invention relates to a clad sheet and a manufacturing method therefor, in particular to a stainless steel clad sheet and a manufacturing method therefor.
  • the stainless steel clad sheet is an integral new material having special composite performances obtained by metallurgical bonding a clad layer on a substrate layer under specific process technology conditions.
  • the stainless steel clad sheet can replace stainless steel to achieve its full performances such as corrosion resistance, heat resistance, hydrogen resistance, wear resistance and brightness, but also has the strength, machinability, weldability and other special performances of carbon steel.
  • the yield strength and tensile strength of the stainless steel composite sheet are low, and the yield strength is often lower than 200MPa, so that the stainless steel composite sheet has its limitations when used in cases where there are higher requirements for mechanical properties.
  • the higher requirements for the performance of stainless steel composite sheets have been put forwarded in the current market, especially in terms of yield strength and surface quality. It is hoped that stainless steel composite sheets can not only meet the requirements of conventional forming and use, but also can have higher yield strength and better surface quality.
  • One of the objectives of the present invention is to provide a high-strength double-sided stainless steel clad sheet, which has high strength, good surface quality and corrosion resistance through reasonable composition design, is suitable for applications in panels, storage tanks and other fields, and saves raw material alloy resources, reduces use cost.
  • the present invention proposes a high-strength double-sided stainless steel clad sheet, which includes a substrate layer and stainless steel clad layers clad-rolled on double sides of the substrate layer; wherein the substrate layer consists of, in mass percent, the chemical elements: C: 0.03-0.12%, 0 ⁇ Si ⁇ 0.30%, Mn: 0.2-1.0%, Al: 0.02-0.04%, Ti: 0.01-0.03%, Nb: 0.005-0.020%, and N: 0.003-0.006%, with the balance being iron and other inevitable impurities.
  • the chemical elements of the substrate layer in mass percent is the chemical elements of a substrate before cladding in mass percent.
  • Carbon is one of the key elements to ensure the strength of steel sheets.
  • the increase in carbon content can increase the strength and hardness of steel. Since the double-sided stainless steel clad sheet is finally subjected to solution treatment, and during the solution treatment, the substrate layer and the stainless steel clad layer undergo high temperature and rapid cooling treatment, so the effect of carbon on the performances of both the substrate layer and the stainless steel clad layer must be considered. Too low carbon content is detrimental to the strength of the substrate layer; and if the carbon content is too high, martensite is easily formed in the substrate layer during heat treatment and rapid cooling, which is unfavorable to the comprehensive mechanical properties of substrate layer and also affects the corrosion resistance of the stainless steel clad layer. Based on this, the inventor of the present invention controls the mass percent of carbon in the substrate layer to 0.03-0.12% to ensure the mechanical properties and elongation performance of the substrate layer and the corrosion resistance of the stainless steel clad layer.
  • Si Adding silicon to steel can improve steel purity and deoxidation effect.
  • silicon plays a role in strengthening solution treatment in steel, but when its mass percent is too high, it is unfavorable to the welding performance of steel.
  • the inventor of the present invention limits the mass percent of silicon in the substrate layer to 0 ⁇ Si ⁇ 0.30%, so as to ensure that the silicon will not affect the corrosion resistance of the stainless steel clad layer, and the substrate layer has good welding performance.
  • Mn The purpose of adding manganese is mainly to increase the strength of steel, and the amount of manganese added mainly depends on the strength level of steel.
  • manganese can also play a deoxidizing role together with aluminum in steel, and the deoxidizing role of manganese can promote the effective effect of titanium, but excessively high manganese content will reduce the plasticity of steel. Therefore, the inventor of the present invention limits the mass percent of manganese in the substrate layer to 0.2-1.0%.
  • Al Aluminum is a strong deoxidizing element. After deoxidation, the excess aluminum and nitrogen in steel can form AlN precipitates, thereby increasing the strength of steel and refining the austenite grain size of steel during heat treatment. In order to ensure that the oxygen content in steel is as low as possible, the inventor of the present invention controls the mass percent of aluminum in the substrate layer to 0.02-0.04%.
  • Titanium is a strong carbide forming element.
  • the addition of a small amount of Ti to steel is beneficial to the fixation of N in steel.
  • the formed TiN can refine the original grain size of austenite in the substrate of the high-strength double-sided stainless steel clad sheet of the present invention, on the other hand, can make the grain size of austenite in the substrate layer not excessively grow during the solutioni treatment of the high-strength double-sided stainless steel clad sheet of the present invention.
  • titanium in steel can also be chemically combined with carbon and sulfur to form TiC, TiS, Ti 4 C 2 S 2 , respectively.
  • the carbide/sulfide precipitates of titanium can prevent the grain growth of the material at the relevant position during solution heat treatment and welding, thereby improving the grain size of the substrate layer after solution treatment and the welding performance of the high-strength double-sided stainless steel clad sheet of the present invention. Therefore, the inventor of the present invention controls the mass percent of titanium in the substrate layer to 0.01-0.03%.
  • Niobium is a strong carbide forming element. A small amount of niobium is added to the substrate layer to increase the recrystallization temperature. In conjunction with the higher solution treatment temperature in the production process, the grains of the substrate layer cannot grow rapidly after solution treatment, which is conducive to good mechanical properties of the substrate layer. Therefore, the inventor of the present invention controls the mass percent of niobium in the substrate layer to 0.005-0.020%.
  • N Nitrogen mainly forms second phase particles with titanium and aluminum to refine grains and improve strength.
  • the mass percent of N is less than 0.003%, there are too few TiN or AlN precipitates to meet the requirements for grain refinement.
  • the mass percent of N is too high, the amount of TiN produced is too large and the grains are too coarse, which will affect the mechanical properties of the substrate layer of the high-strength double-sided stainless steel clad sheet of the present invention. Therefore, the inventor of the present invention controls the mass percent of nitrogen in the substrate layer to 0.003-0.006%.
  • P and S are harmful impurity elements in steel.
  • Phosphorus will seriously damage the plasticity and toughness of steel sheets.
  • Sulfur will chemically combine with manganese in steel to form plastic inclusions, namely manganese sulfide, which is especially harmful to the transverse plasticity and toughness of steel, therefore, the content of P and S in steel is reduced as much as possible.
  • the present invention limits the mass percent of P and S in the substrate layer to P ⁇ 0.02% and S ⁇ 0.015%.
  • the average composition of each element in the transition layers is between the corresponding composition of the element in the substrate layer and the corresponding composition of the element in the stainless steel clad layer in a gradient transition, for example, alloying elements with a higher mass percent (such as Cr, Ni) in the stainless steel clad layer diffuse to the substrate layer, and carbon with a higher mass percent in the substrate layer diffuses to the stainless steel clad layer, and therefore the average compositions of C, Cr and Ni in the transition layers are between those in the stainless steel clad layer and the substrate layer.
  • the chemical elements in the substrate layer also satisfy: 2.7 ⁇ C+0.4 ⁇ Si+Mn ⁇ 1.25, wherein C, Si and Mn each present respective mass percent of themself.
  • the formula can ensure that the substrate obtains the microstructure of ferrite + pearlite + bainite, or ferrite + pearlite + bainite + widmanstatten in a certain process window range.
  • the microstructure of the substrate layer is ferrite + pearlite + bainite, or ferrite + pearlite + bainite + widmanstatten, wherein the phase proportion of the bainite is ⁇ 20%, and the phase proportion of the widmanstatten is ⁇ 10%.
  • the transition layers exist on the upper and lower surfaces of the substrate layer, carbon-poor zones caused by the diffusion of carbon exist in the range of 0-100 ⁇ m on the upper and lower surfaces of the substrate layer in the thickness direction of the substrate layer, and forming a ferrite zone with a thickness of 50-100 ⁇ m in the substrate layer, and the substrate and the clad sheet are metallurgically bonded.
  • the yield strength at room temperature is ⁇ 300MPa
  • the elongation at room temperature is ⁇ 30%
  • the value of yield platform during mechanical stretching is ⁇ 2.0%.
  • the stainless steel clad layer is an austenitic stainless steel clad layer.
  • the austenitic stainless steel is Cr-Ni based stainless steel or Cr-Ni-Mo based stainless steel.
  • the total thickness of the double-sided stainless steel clad layer accounts for 10%-30% of the total thickness of the high-strength double-sided stainless steel clad sheet, and the stainless steel clad layer on the upper and lower surfaces of the substrate layer is set to be symmetrical or asymmetrical in thickness.
  • another objective of the present invention is to provide a manufacturing method for the above-mentioned high-strength double-sided stainless steel clad sheet.
  • the high-strength double-sided stainless steel clad sheet obtained by the manufacturing method has high strength, good surface quality and corrosion resistance, is suitable for applications in panels, storage tanks and other fields, and saves raw material alloy resources, reduces use cost.
  • the present invention proposes a manufacturing method for the above-mentioned high-strength double-sided stainless steel clad sheet, which includes the steps:
  • the stainless steel clad layer can be obtained by using the process of prior art, for example, Cr-Ni or Cr-Ni-Mo based austenitic stainless steel is subjected to steelmaking, continuous casting, rolling, solution annealing, precision cutting, and pickling to make the stainless steel clad layer to be used in the subsequent billet making process.
  • a substrate layer billet can be obtained first, and then the substrate layer billet can be used as the substrate layer to make assemble billet with the stainless steel clad layer in the subsequent steps; or the substrate layer billet can be obtained first, and then the substrate layer billet is subjected to cogging and rolling to obtain a substrate layer steel sheet, which is used as the substrate layer to make assemble billet with the stainless steel clad layer in the subsequent steps.
  • step (2) in some preferred embodiments, pretreatment is performed before the billet making to ensure that there is no contamination on the stainless steel clad surface.
  • the solution temperature is controlled to be 950-1020°C.
  • the solution temperature is lower than 950°C, recrystallization and softening of austenitic stainless steel of the stainless steel clad layer cannot occur sufficiently, and the carbides that partially precipitate cannot be sufficiently solution treated; and when the solution treatment temperature is higher than 1020°C, the carbon steel grain structure of the substrate layer may grow rapidly, and in the subsequent rapid cooling process, it is easy to form a large amount of widmanstatten structure.
  • controlling the cooling rate after solution treatment in the range of 20-50°C/s can ensure that the carbides that are dissolved in the stainless steel clad layer may not precipitate during subsequent cooling, and on the other hand, can ensure that the microstructure of the substrate layer is ferrite + pearlite + a small amount of bainite, and avoid the appearance of martensite structure, thereby ensuring good comprehensive mechanical properties of the high-strength double-sided stainless steel clad sheet of the present invention.
  • the method further includes:
  • the solution temperature is controlled to be 950-1020°C.
  • the solution temperature is lower than 950°C, recrystallization and softening of austenitic stainless steel of the stainless steel clad layer cannot occur sufficiently, and the carbides that partially precipitate cannot be sufficiently solution treated; and when the solution temperature is higher than 1020°C, the carbon steel grain structure of the substrate layer may grow rapidly, and in the subsequent rapid cooling process, it is easy to form a large amount of widmanstatten structure.
  • controlling the cooling rate after solution treatment in the range of 20-50°C/s can ensure that the carbides that are dissolved in the stainless steel clad layer may not precipitate during subsequent cooling, and on the other hand, can ensure that the microstructure of the substrate layer is ferrite + pearlite + a small amount of bainite and avoid the appearance of martensite structure, thereby ensuring good comprehensive mechanical properties of the high-strength double-sided stainless steel clad sheet of the present invention.
  • the high-strength double-sided stainless steel clad sheet and the manufacturing method therefor have the following beneficial effects.
  • Table 1-1 and Table 1-2 list the mass percent of each chemical element in substrate layers of high-strength double-sided stainless steel clad sheets and models of stainless steel clad layers of Examples 1-8 and Comparative Example 1.
  • stainless steel clad layers of the high-strength double-sided stainless steel clad sheets of Examples 1-8 and Comparative Example 1 are all stainless steels that are available in the prior art. Therefore, Tables 1-1 and 1-2 only list the specific models of the stainless steel clad layers, and the composition of various chemical elements will not be recorded.
  • F represents ferrite
  • P represents pearlite
  • B represents bainite
  • W represents widmanstatten structure
  • Example 1 Mechanical tensile properties at room temperature Value of yield platform (%) Yield strength (MPa) Tensile strength (MPa) Elongation rate (A 50 , %) Example 1 355 510 39.0 0.5 Example 2 390 540 36.0 none Example 3 375 553 32.0 none Example 4 375 505 38.0 0.5 Example 5 420 560 30.0 none Example 6 300 480 33.0 2.0 Example 7 385 590 31.0 none Example 8 405 530 34.0 none Comparative Example 1 217 439 48.0 none
  • the high-strength double-sided stainless steel clad sheets of Examples 1-8 have the yield strength of 300MPa or above, which is 83-203MPa higher than the yield strength of the high-strength double-sided stainless steel clad sheet of Comparative Example 1, and have better surface quality, which meets the requirements of market users for good surface quality and higher yield strength.
  • the microstructure of the substrate layer of the high-strength double-sided stainless steel clad sheet of Example 4 is F+P+B, and the grain size of F is about grade 7.
  • the microstructure of the stainless steel clad layer of the high-strength double-sided stainless steel clad sheet of Example 4 is a completely recrystallized austenite grain structure.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Pressure Welding/Diffusion-Bonding (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Laminated Bodies (AREA)
EP19803939.8A 2018-05-16 2019-05-15 Panneau composite en acier inoxydable double paroi de haute résistance et son procédé de fabrication Pending EP3778976A4 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
CN201810468895.XA CN110499453B (zh) 2018-05-16 2018-05-16 一种高强双面不锈钢复合板及其制造方法
PCT/CN2019/087080 WO2019219031A1 (fr) 2018-05-16 2019-05-15 Panneau composite en acier inoxydable double paroi de haute résistance et son procédé de fabrication

Publications (2)

Publication Number Publication Date
EP3778976A1 true EP3778976A1 (fr) 2021-02-17
EP3778976A4 EP3778976A4 (fr) 2021-06-16

Family

ID=68539502

Family Applications (1)

Application Number Title Priority Date Filing Date
EP19803939.8A Pending EP3778976A4 (fr) 2018-05-16 2019-05-15 Panneau composite en acier inoxydable double paroi de haute résistance et son procédé de fabrication

Country Status (8)

Country Link
US (1) US11833777B2 (fr)
EP (1) EP3778976A4 (fr)
JP (1) JP7274505B2 (fr)
KR (1) KR20210002621A (fr)
CN (1) CN110499453B (fr)
AU (1) AU2019271821B2 (fr)
CA (1) CA3099932C (fr)
WO (1) WO2019219031A1 (fr)

Families Citing this family (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN112877589B (zh) * 2019-11-29 2022-03-18 宝山钢铁股份有限公司 一种碳钢奥氏体不锈钢轧制复合板及其制造方法
CN113106327B (zh) * 2020-01-13 2022-06-24 宝山钢铁股份有限公司 一种高耐蚀带钢及其制造方法
JP7474079B2 (ja) 2020-03-12 2024-04-24 日鉄ステンレス株式会社 クラッド鋼板およびその製造方法
CN111687234B (zh) * 2020-05-06 2022-06-14 山西太钢不锈钢股份有限公司 不锈钢特厚板制造方法
CN111876685B (zh) * 2020-08-06 2021-10-22 东北大学 一种屈服强度555MPa级高韧性管线钢及其生产方法
CN112501422A (zh) * 2020-11-27 2021-03-16 山西太钢不锈钢股份有限公司 304系高档面板不锈钢原料表面处理方法
CN113444865A (zh) * 2021-05-10 2021-09-28 北京交通大学 一种双相不锈钢-碳钢复合板的热处理工艺方法
CN115927972B (zh) * 2022-12-05 2024-01-30 襄阳金耐特机械股份有限公司 一种奥氏体耐热不锈钢

Family Cites Families (26)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS6043433A (ja) * 1983-08-19 1985-03-08 Nippon Kokan Kk <Nkk> 耐食性および靭性に優れたクラツド鋼板の製造方法
JPS6259034A (ja) * 1985-05-29 1987-03-14 新日本製鐵株式会社 加工性および耐食性の優れたステンレスクラッド鋼板
DE3742539A1 (de) 1987-12-16 1989-07-06 Thyssen Stahl Ag Verfahren zur herstellung von plattiertem warmband und danach hergestelltes plattiertes warmband
JP2510783B2 (ja) * 1990-11-28 1996-06-26 新日本製鐵株式会社 低温靭性の優れたクラッド鋼板の製造方法
JP2737525B2 (ja) * 1992-03-06 1998-04-08 日本鋼管株式会社 母材の脆性破壊伝播停止特性に優れたオーステナイト系ステンレスクラッド鋼板の製造方法
JP2663089B2 (ja) * 1993-03-08 1997-10-15 新日本製鐵株式会社 耐食性と低温靱性に優れた複合鋼板
JPH07305140A (ja) * 1994-05-11 1995-11-21 Nippon Steel Corp 低温靱性と耐食性に優れた複合鋼板
JPH1177888A (ja) * 1997-09-02 1999-03-23 Nkk Corp ステンレスクラッド鋼板
JPH11152547A (ja) 1997-11-19 1999-06-08 Nkk Corp 耐二次加工脆性に優れた薄板ステンレスクラッド鋼板
JP4674421B2 (ja) 2001-07-13 2011-04-20 Ｊｆｅスチール株式会社 高耐食クラッド鋼板の製造方法
US7653999B2 (en) * 2005-03-31 2010-02-02 Babcock & Wilcox Canada Ltd. Co-extruded generating bank swaged tubing
EP2702178A1 (fr) 2011-04-27 2014-03-05 Tata Steel Nederland Technology B.V. Composite de feuillard en acier et son procédé de fabrication
KR101301994B1 (ko) 2011-11-16 2013-09-03 삼성중공업 주식회사 선박용 클래드강 제조 방법
JP5418662B2 (ja) * 2012-01-30 2014-02-19 Ｊｆｅスチール株式会社 溶接部靭性に優れた高靭性クラッド鋼板の母材及びそのクラッド鋼板の製造方法
CN102825858B (zh) * 2012-09-19 2015-06-24 太原钢铁(集团)有限公司 一种核电工程用复合钢板及其制备方法
JP6256905B2 (ja) * 2013-06-07 2018-01-10 株式会社 資生堂 香料内包カプセル及びそれを配合した化粧料
WO2015059909A1 (fr) 2013-10-21 2015-04-30 Ｊｆｅスチール株式会社 Tôle d'acier pour placage à base d'acier inoxydable austénitique et son procédé de fabrication
CN104441822A (zh) * 2014-11-29 2015-03-25 首钢总公司 一种不锈钢与碳钢复合钢板及其生产方法
JP6168131B2 (ja) * 2014-12-09 2017-07-26 Ｊｆｅスチール株式会社 ステンレスクラッド鋼板
CN104760351A (zh) * 2015-04-07 2015-07-08 首钢总公司 一种碳钢与奥氏体不锈钢复合钢板及其生产方法
CN104988414A (zh) * 2015-06-20 2015-10-21 秦皇岛首秦金属材料有限公司 一种强韧性能的碳钢与不锈钢复合钢板及生产方法
JP6390567B2 (ja) 2015-09-24 2018-09-19 Ｊｆｅスチール株式会社 ステンレスクラッド鋼板の製造方法
CN105296854B (zh) * 2015-09-25 2021-02-19 宝钢德盛不锈钢有限公司 一种具有优良综合性能的冷轧双面不锈钢复合板及制造方法
CN105245658A (zh) 2015-11-01 2016-01-13 陀金荣 潜水船带万向节手机套
CN107226301B (zh) 2016-05-30 2019-09-13 南通中集罐式储运设备制造有限公司 罐式集装箱及其罐体
CN106269961A (zh) * 2016-08-29 2017-01-04 山东钢铁股份有限公司 一种集装箱用不锈钢双面复合板及其制造方法

Also Published As

Publication number Publication date
CN110499453B (zh) 2021-09-17
CN110499453A (zh) 2019-11-26
AU2019271821A1 (en) 2020-12-03
AU2019271821B2 (en) 2021-11-04
WO2019219031A1 (fr) 2019-11-21
CA3099932A1 (fr) 2019-11-21
EP3778976A4 (fr) 2021-06-16
JP2021523301A (ja) 2021-09-02
JP7274505B2 (ja) 2023-05-16
US11833777B2 (en) 2023-12-05
US20210213709A1 (en) 2021-07-15
CA3099932C (fr) 2023-09-19
KR20210002621A (ko) 2021-01-08

Similar Documents

Publication Publication Date Title
US11833777B2 (en) High-strength double-sided stainless steel clad sheet and manufacturing method therefor
KR100851158B1 (ko) 충돌특성이 우수한 고망간형 고강도 강판 및 그 제조방법
EP3309276A1 (fr) Tôle d&#39;acier ultra-épaisse à faible susceptibilité à la fissuration et faible rapport de la limite d&#39;élasticité sur la contrainte à la rupture et son procédé de fabrication
US11339451B2 (en) Low-cost and high-formability 1180 MPa grade cold-rolled annealed dual-phase steel plate and manufacturing method thereof
EP3653736B1 (fr) Bande d&#39;acier laminée à chaud et procédé de fabrication
JP2019524986A (ja) 強度及び成形性に優れたクラッド鋼板及びその製造方法
JP2011208226A (ja) 延性に優れた高張力鋼板およびその製造方法
US20220396054A1 (en) High corrosion-resistance strip steel and manufacturing method therefor
CN113416889B (zh) 焊接性能良好超高强热镀锌dh1470钢及制备方法
EP4206348A1 (fr) Acier à expansion ultra-élevée de qualité 780 mpa ayant une qualité de surface élevée et une stabilité de performance élevée, et son procédé de fabrication
KR101439613B1 (ko) 굽힘 가공성과 연신율이 우수한 고강도 고망간 강판 및 그 제조방법
EP2434029B1 (fr) Feuille d&#39;acier ultra-fine et procédé de fabrication de celle-ci
CN108728728B (zh) 一种具有极低屈强比的高锰钢及其制造方法
CN108690939B (zh) 一种高成形含氮奥氏体不锈钢及其制造方法
KR101778404B1 (ko) 강도 및 성형성이 우수한 클래드 강판 및 그 제조방법
US20220410533A1 (en) Multi-layer rolled composite board and manufacturing method therefor
JPS6366368B2 (fr)
JPH08199293A (ja) 亀裂伝播停止特性に優れた耐サワー鋼板
CN104726780A (zh) 一种高强度特厚钢板及其生产方法
US11130161B2 (en) High-strength corrosion-resistant composite chequered iron and manufacturing method therefor
JP2012214897A (ja) 耐加工肌荒れ性に優れるフェライト系ステンレス鋼板
CN110331339B (zh) 一种低温韧性优异的高强度钢板及其制造方法
CN102127704B (zh) 900MPa级高强度高塑性中碳热轧钢及其制造方法
CN114480949A (zh) 一种690MPa级低屈强比耐候焊接结构钢、钢板及其制造方法
JP2007277729A (ja) 高強度溶融亜鉛メッキ鋼板およびその製造方法

Legal Events

Date Code Title Description
STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: THE INTERNATIONAL PUBLICATION HAS BEEN MADE

PUAI Public reference made under article 153(3) epc to a published international application that has entered the european phase

Free format text: ORIGINAL CODE: 0009012

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: REQUEST FOR EXAMINATION WAS MADE

17P Request for examination filed

Effective date: 20201110

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR

AX Request for extension of the european patent

Extension state: BA ME

A4 Supplementary search report drawn up and despatched

Effective date: 20210518

RIC1 Information provided on ipc code assigned before grant

Ipc: B32B 15/01 20060101AFI20210511BHEP

Ipc: C22C 38/02 20060101ALI20210511BHEP

Ipc: C22C 38/04 20060101ALI20210511BHEP

Ipc: C22C 38/06 20060101ALI20210511BHEP

Ipc: C22C 38/12 20060101ALI20210511BHEP

Ipc: C22C 38/14 20060101ALI20210511BHEP

Ipc: C22C 38/00 20060101ALI20210511BHEP

Ipc: C22C 38/40 20060101ALI20210511BHEP

Ipc: C22C 38/44 20060101ALI20210511BHEP

Ipc: C21D 8/02 20060101ALI20210511BHEP

Ipc: C21D 9/46 20060101ALI20210511BHEP

Ipc: C21D 6/00 20060101ALI20210511BHEP

Ipc: C22C 33/04 20060101ALI20210511BHEP

DAV Request for validation of the european patent (deleted)
DAX Request for extension of the european patent (deleted)
STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: EXAMINATION IS IN PROGRESS

17Q First examination report despatched

Effective date: 20211209